High strength steel sheet and method for manufacturing the same

ABSTRACT

The present invention relates to a high strength steel sheet consisting essentially of 0.04 to 0.1% C, 0.5% or less Si, 0.5 to 2% Mn, 0.05% or less P, 0.005% or less O, 0.005% or less S, by weight, having 10 μm or less of average ferritic grain size, and 20 mm/mm 2  or less of generation frequency A, which generation frequency A is defined as the total length of a banded secondary phase structure observed per 1 mm 2  of steel sheet cross section along the rolling direction thereof. The steel sheet is manufactured by, for example, a method comprising the steps of: hot-rolling a continuously cast slab having the composition described above at temperatures of Ar 3  transformation point or above directly or after reheating thereof; and cooling the hot-rolled steel sheet within 2 seconds down to the temperatures of from 600 to 750° C. at cooling speeds of from 100 to 2,000° C./sec, followed by coiling the cooled steel sheet at temperatures of from 450 to 650° C. The present invention provides a high strength steel sheet having strengths of 340 MPa or more and having excellent stretch flanging performance, ductility, and shock resistance, providing a sufficient coil shape with good surface properties, even when hot dip zinc-coating is applied.

This Application is a Continuation Application of application Ser. No. 10/625,796 filed Jul. 23, 2003, now pending, which is a Divisional Application of application Ser. No. 09/827,597 filed Apr. 5, 2001, now U.S. Pat. No. 6,663,725 B2, which is a Continuation Application of International Application PCT/JP00/06252 filed Sep. 13, 2000 (not published in English) which is hereby incorporated in its entirety herein by this reference.

BACKGROUND OF THE INVENTION

1. Field of the Invention

The present invention relates to a high strength steel sheet having 340 MPa or higher strength and giving excellent stretch flanging performance, ductility, shock resistance, surface properties, and other characteristics, and relates to a method for manufacturing the same.

2. Description of Related Art

Steel sheets such as hot-rolled steel sheets and cold-rolled steel sheets are press-worked in various shape members for use in the fields of automobiles, household electric appliances, industrial machines, and the like. In recent years, manufacturers of automobiles and other products have increased their use rate of high strength steel sheets responding to the need of weight reduction.

The high strength steel sheets have, however, problems such as the stretch flanging cracks occurred when the high strength steel sheets having 340 MPa or higher strength are treated by burring, the workability issue such as insufficient ductility of high strength hot dip zinc-coated steel sheets having 440 MPa or higher strength, and the issue of insufficient shock resistance which is important to secure safety on collision. Those types of high strength steel sheets having 340 MPa or higher strength are manufactured using the base carbon steel being adjusted in carbon equivalent to 0.05 to 0.2 wt. % C, adding precipitation-strengthening elements such as Ti, Nb, and V responding to the strength thereof. When, however, the steels of these compositions are hot-rolled, cracks likely occur, which degrades the surface properties to significantly reduce the production yield.

As the technologies for improving the workability of high strength steel sheets, JP-B-61-15929 and JP-B-63-67524, (the term “JP-B” referred herein signifies “Examined Japanese Patent Publication”), for example, disclose the method to improve the balance of strength and ductility, the breaking elongation (ductility), and the toughness by controlling the cooling speed after hot-rolling and the coiling temperature. As the technology to improve the stretch flanging performance, Japanese Patent No. 2555436 discloses the method for manufacturing steel sheet having strengths of from 500 to 600 MPa and having excellent stretch flanging performance, which steel sheet is prepared by hot-rolling a Ti-added steel, by cooling the steel sheet at cooling speeds of from 30 to 150° C./sec, and by coiling the steel sheet at temperatures of from 250 to 540° C. to establish a (ferrite+bainite) structure. JP-B-7-56053 discloses the method for manufacturing hot dip zinc-coated steel sheet having strengths of from 450 to 500 MPa and having excellent stretch flanging performance, which steel sheet is prepared by cooling a hot-rolled steel sheet at cooling speeds of 10° C./sec or more to establish a (ferrite+pearlite) structure. JP-A-4-88125, (the term “JP-A” referred herein signifies “Unexamined Japanese Patent Publication”), discloses the method for manufacturing steel sheet having strengths of from 500 to 700 MPa and having excellent stretch flanging performance, which steel sheet is prepared by hot-rolling a Ca-added steel at temperatures of from (Ar₃ transformation point+60° C.) to 950° C., by cooling the steel sheet within 3 seconds after completed the hot-rolling down to the temperature range of from 410 to 620° C. at cooling speeds of 50° C./sec or more, by cooling the steel sheet in air, and by coiling the steel sheet at temperatures of from 350 to 500° C. to establish a (ferrite+pearlite) structure. JP-A-7-54051 discloses the method for manufacturing high strength hot dip zinc-coated steel sheet having excellent stretch flanging performance and ductility, which steel sheet is prepared by hot-rolling a Nb—Ti added steel at temperatures ranging from 850 to 1,000° C., by cooling the hot-rolled steel sheet down to 600° C. at average cooling speeds of 40° C./sec or more, by further cooling the steel sheet at average cooling speeds of 30° C./sec or less, by coiling the steel sheet at temperatures of from 400 to 550° C., and by applying hot dip zinc-coating.

The methods described in these prior arts, however, have problems of unable to completely prevent the stretch flanging cracks occurred during burring treatment, of not necessarily unable to assure excellent shock resistance, and of giving insufficient coil shape when the coiling temperature becomes to below 400° C. caused from low ductility. For the case of hot dip zinc-coated steel sheet, there are several problems on attaining satisfactory ductility, including the problems of limitation on added amount of Si which is effective to improve ductility, and of unable to apply (ferrite+martensite) structure which is effective in ductility improvement for the use requiring high yield ratio.

SUMMARY OF THE INVENTION

The present invention was completed to solve the above-described problems, and an object of the present invention is to provide a high strength steel sheet having 340 MPa or higher strength and providing excellent stretch flanging performance, ductility, and shock resistance, and giving a sufficient coil shape and favorable surface properties even under hot dip zinc-coating treatment.

The object of the present invention is attained by a high strength steel sheet consisting essentially of 0.04 to 0.1% C, 0.5% or less Si, 0.5 to 2% Mn, 0.05% or less P, 0.005% or less O, 0.005% or less S, by weight, having 10 μm or less of average ferritic grain size, and 20 mm/mm² or less of generation frequency A, which generation frequency A is defined as the total length of a banded secondary phase structure observed per 1 mm² of steel sheet cross section along the rolling direction thereof.

The high strength steel sheet is prepared by a manufacturing method comprising the steps of: hot-rolling a continuously cast slab having the composition described above at temperatures of Ar₃ transformation point or above directly or after reheating thereof; and cooling the hot-rolled steel sheet within 2 seconds down to the temperatures of from 600 to 750° C. at cooling speeds of from 100 to 2,000° C./sec, followed by coiling the cooled steel sheet at temperatures of from 450 to 650° C.

In particular, to further improve the ductility of high strength hot dip zinc-coated steel sheet having strengths of 440 MPa or more, it is preferred to apply a manufacturing method comprising the steps of: hot-rolling a steel slab consisting essentially of 0.01 to 0.3% C, 0.7% or less Si, 1 to 3% Mn, 0.08% or less P, 0.01% or less S, 0.08% or less sol.Al, and 0.007% or less N, by weight, at temperatures of Ar₃ transformation point or above; cooling the hot-rolled steel sheet within 2.5 seconds down to the temperatures ranging from above 500° C. to 700° C. at average cooling speeds of 100° C./sec or more, followed by coiling the cooled steel sheet; and pickling or cold-rolling after pickling the coiled steel sheet, then annealing thereto in a continuous hot dip zinc-coating line at temperatures of 720° C. or above to perform the zinc coating.

For completely preventing the degradation of surface properties caused from the cracks generated during hot-rolling, it is preferred to apply a manufacturing method comprising the steps of: hot-rolling a continuously cast slab consisting essentially of 0.05 to 0.2% C, 0.15% or less Si, 0.4 to 2.0% Mn, 0.025% or less P, 0.005% or less O, 0.01% or less S, 0.006% or less N, and 0.004% or less Sn, by weight, and having Mn/S≧50 at temperatures of Ar₃ transformation point or above directly or after reheating the continuously cast slab; and cooling the hot-rolled steel sheet down to the temperatures of from 400° C. to 700° C. at cooling speeds of from 20 to 2,000° C./sec, followed by coiling the cooled steel sheet.

BRIEF DESCRIPTION OF THE DRAWINGS

FIG. 1 is a graph showing the relation between TS×El, TS×λ, average ferritic grain size, and generation frequency A of banded secondary phase structure.

FIG. 2 is a graph showing the relation between primary cooling speed, TS×El, and TS×λ.

FIG. 3 is a graph showing the relation between primary cooling speed and El.

FIG. 4 is a graph showing the relation between TS, λ, and surface properties.

FIG. 5 is a graph showing the relation between TS, λ, and surface properties.

FIG. 6 is a graph showing the relation between TS, λ, and surface properties.

DETAILED DESCRIPTION OF PHE INVENTION Embodiment 1

The inventors of the present invention conducted detail study on the stretch flanging performance, the ductility, and the shock resistance of high strength steel sheets, and found that the elimination of the banded secondary phase structure existing over the whole range of the sheet thickness caused from the enrichment of C, Mn, and other elements is effective to improve the stretch flanging performance and the ductility, and that the increase of the yield strength of the steel sheet within a range not to degrade the workability of the steel sheet is effective to improve the shock resistance.

The high strength steel sheet according to the present invention was completed based on the findings. The following is the detail description of the present invention.

1. Composition

Carbon is an element necessary to assure the strength. If the C content is less than 0.04%, the strength of 340 MPa or more cannot be obtained. If the C content exceeds 0.1%, the workability degrades. Accordingly, the C content is specified to a range of from 0.04 to 0.1%.

Silicon is an element to strengthen by solid solution and an element necessary to assure the strength. If the Si content exceeds 0.5%, the surface properties degrade. Consequently, the Si content is specified to 0.5% or less.

Manganese is an element to strengthen by solid solution and is an effective element for improving the toughness. If the Mn content is less than 0.5%, the effect cannot be attained. If the Mn content exceeds 2%, the degradation of workability becomes significant. Therefore, the Mn content is specified to a range of from 0.5 to 2%.

Phosphorus is an element to strengthen by solid solution. If the P content exceeds 0.05%, the segregation thereof induces the degradation of workability. Thus, the P content is specified to 0.05% or less.

Oxygen above 0.005% content likely induces the cracks on the surface or below the surface of slab during continuous casting. Therefore, the O content is specified to 0.005% or less.

Sulfur above 0.005% content leads to the increase in sulfide and degrades the workability. Consequently, the S content is specified to 0.005% or less. In particular, for establishing good balance of strength and stretch flanging performance, the S content is preferably specified to 0.003% or less.

2. Structure

In a hot-rolled steel sheet, a hot-rolled steel sheet-treated by alloyed hot dip zinc-coating, a hot-rolled steel sheet treated by cold-rolling followed by alloyed hot dip zinc-coating, and the like, ferritic grains are preferably in small size as far as possible by finely dispersing the secondary phase structure of carbide, pearlite, bainite, martensite, austenite, and the like to assure good balance of strength and ductility. When that type of secondary phase structure is formed in banded pattern, the balance of strength and elongation degrades.

When the total length of the banded secondary phase structure observed per 1 mm² of sheet cross sectional area along the rolling direction is defined as the generation frequency A, it is found that, as shown in FIG. 1, in the case of 10 μm or less of average ferritic grain size and of 20 mm/mm² or less of generation frequency A, excellent balance of strength and ductility (TS×El) and balance of strength and stretch flanging performance (TS×λ) can be attained. The term A signifies the hole expanding rate normally used for evaluating the stretch flanging performance. The range of generation frequency A of 20 mm/mm² or less includes the case of 0 mm/mm², that is, the case in which no secondary phase structure is observed.

Furthermore, since the yield strength of the high strength steel sheet according to the present invention is increased by refining ferritic grains and secondary phase structure, the shock resistance is also excellent.

The high strength steel sheet according to the present invention may further contain 0.01 to 0.3% as the sum of at least one element selected from the group consisting of Ti, Nb, V, Mo, and Cr, adding to the above-described components, to improve the strength.

When the high strength steel sheet according to the present invention is regulated in the variations of tensile strength in the width direction and in the longitudinal direction of the steel sheet to within ±8% to the average value thereof, preferably within ±4%, and more preferably within ±2%, the variations of workability such as spring back during bending work can be significantly reduced.

The high strength steel sheet according to the present invention can be prepared by, for example, a manufacturing method comprising the steps of: hot-rolling a continuously cast slab having the above-described composition at temperatures of Ar₃ transformation point or above directly or after reheating thereof; and cooling the hot-rolled steel sheet within 2 seconds down to the temperatures ranging from 600 to 750° C. at cooling speeds of from 100 to 2,000° C./sec, followed by coiling the cooled steel sheet at temperatures ranging from 450 to 650° C.

The hot-rolling can be conducted by rolling the continuously cast slab in as-cast state or by rolling after reheating. It is, however, necessary to complete the rolling at temperatures of Ar₃ transformation point or above to refine the ferritic grains and the secondary phase structure after the transformation, to improve the balance of strength and ductility of steel sheet, and to improve the balance of strength and stretch flanging performance thereof. In that case, when the continuously cast slab is reheated, it is preferable to heat the slab to 1,250° C. or below.

After the hot-rolling, it is necessary to apply cooling (primary cooling) within 2 seconds at cooling speeds of from 100 to 2,000° C./sec to refine the ferritic grains and the secondary phase structure after the transformation and to improve the stretch flanging performance by bringing the generation frequency A, as the total length of the above-described secondary phase structure, to 20 mm/mm² or less. If the cooling starts after longer than 2 seconds from hot-rolling, the ferritic grains and the secondary phase structure cannot be refined. From the point of suppression of the formation of banded secondary phase structure, it is preferable to homogenize the austenite structure before the transformation. To do this, the cooling is preferably started after more than 0.5 second. If the cooling speed is less than 100° C./sec, the structure formation responding to the C and Mn enriched section formed during the solidification proceeds to likely form the banded secondary phase structure, which fails to establish 20 mm/mm² or less of generation frequency A. If the cooling speed is 100° C./sec or more, higher cooling speed is more preferred, and, 200° C./sec or more, further 400° C./sec or more is preferable. From the industrial application view, however, the upper limit of the cooling speed is 2,000° C./sec.

With the end temperature of cooling with that level of cooling speed, if the temperature is above 750° C., the ferritic grains are not refined to result in nonuniform dispersion of the secondary phase, as seen in FIG. 2, thus lowering the value of TS×λ, and, if the temperature is below 600° C., the secondary phase becomes a hard low temperature transformed phase, which lowers the value of TS×El. Therefore, the temperature is necessary to be between 600 and 750° C.

After that, for example, it is necessary to apply the cooling (secondary cooling) at approximate cooling speeds of less than 50° C./sec, and to apply the coiling of the steel sheet at temperatures of from 450 to 650° C. The reason is that coarse pearlite harmful to ductility is formed at temperatures higher than 650° C., and that low temperature transformed phase harmful to workability is formed at temperatures below 450° C. To establish homogeneous mechanical properties, the difference in coiling temperatures in a coil is preferably to set within 50° C.

When the coiled steel sheet is pickled and annealed, or pickled, cold-rolled, and annealed, the manufactured high strength hot-rolled steel sheet and high strength cold-rolled steel sheet have further excellent balance of strength and ductility, balance of strength and stretch flanging, and shock resistance.

To assure the above-described generation frequency A of 20 mm/mm² or less, it is preferred to suppress segregation of elements such as Mn and C through the treatment to reduce segregation during the continuous casting by separate or combined electromagnetic agitation, slight drafting casting, rapid cooling of slab, and the like.

When the variations in temperature in the width direction and in the longitudinal direction of the steel sheet after cooled at cooling speeds of from 100 to 2,000° C./sec to a temperature range of 60° C. or less through the cooling with 2,000 kcal/m²h° C. or higher heat transfer coefficient, the above-described high strength steel sheet having within ±8% of the above-described tensile strength to the average value can be manufactured. To attain the variations of tensile strength within ±4% or ±2% to the average value, the cooling is conducted with the heat transfer coefficients of 5,000 kcal/m²h° C. or more or 8,000 kcal/m²h° C. or more to control the variations of above-described temperature within 40° C. or 20° C., respectively. The cooling with that high level of heat transfer coefficient is difficult to be realized in conventional laminar cooling process. However, the perforated ejection type cooling process can realize the cooling.

For further reducing the variations of temperature after the cooling at cooling speeds of from 100 to 2,000° C./sec, it is effective to install an induction heating unit at inlet side of the finish-rolling mill or between stands of the finish-rolling mill to heat the steel sheet under rolling to conduct the temperature adjustment. In a continuous hot-rolling process using a coil box, the heating of the steel sheet may be done before or after the coil box, between the stands of the rough-rolling mill, or before or after the welder.

The high strength steel sheet according to the present invention can be treated by hot dip zinc-coating. In that case, the annealing temperature is preferably in a range of from 650 to 850° C. in view of improvement of ductility.

EXAMPLE 1

Steel having the chemical composition given in Table 1 was prepared by melting. The steel was rolled under the conditions given in Table 2 to form hot-rolled steel sheets Nos. 1 through 6, each having a thickness of 2.3 mm. The hot-rolled steel sheets Nos. 1 through 4 were treated by segregation reduction during the slab casting. After that, the hot-rolled steel sheet No. 3 was treated by pickling, cold-rolling, and hot dip zinc-coating. The hot-rolled steel sheet No. 4 was treated by pickling and hot dip zinc-coating. Mechanical properties were determined on the steel sheets Nos. 1, 2, 5, and 6 which were left as-hot-rolled state, the steel sheet No. 3 as the hot dip zinc-coated cold-rolled steel sheet, and the steel sheet No. 4 as the hot dip zinc-coated hot-rolled steel sheet. The stretch flanging performance was evaluated by the hole expanding rate λ determined by opening a hole of 10 mm in diameter with 12% of clearance on the steel sheet, and by expanding the hole from the burr formation side using a conical punch.

The result is shown in Table 3.

The steel sheets Nos. 1 through 4 and 6 as Examples of the present invention give superior balance of strength and ductility and balance of strength and stretch flanging performance to the steel sheet No. 5 as a Comparative Example treated by the primary cooling speed, after the hot-rolling, of outside the range of the present invention, and give high yield strength and excellent shock resistance. In particular, for the steel sheets Nos. 1 through 4 which were treated to reduce segregation during the continuous casting provide high value of λ and excellent stretch flanging performance. TABLE 1 Composition (wt. %) C Si Mn S P O N 0.056 0.01 1.25 0.002 0.014 0.0025 0.0036

TABLE 2 Finishing Time to start Primary End temperature Secondary Steel Slab temperature of the primary cooling of the primary cooling sheet Heat-treatment Treatment to rolling cooling speed cooling speed No. history reduce segregation (° C.) (sec) (° C./sec) (° C.) (° C./sec) Remark 1 Casting, then Applied Ar₃ − (Ar₃ + 25) 1.3 210 640 35 Example heating to 1,250° C. 2 Casting, then Applied Ar₃ − (Ar₃ + 30) 0.5 205 680 40 Example heating to 1,250° C. 3 Casting, then Applied Ar₃ − (Ar₃ + 25) 0.6 210 640 45 Example heating to 1,250° C. 4 Casting, then Applied Ar₃ − (Ar₃ + 30) 0.6 205 640 40 Example heating to 1,250° C. 5 Casting, then Applied (Ar₃ + 10) − (Ar₃ + 35) 0.5  30* 705 40 Comparative heating to 1,250° C. example 6 Casting, then Not applied (Ar₃ + 10) − (Ar₃ + 30) 0.6 200 650 35 Example heating to 1,250° C. *Outside of the range of the present invention

TABLE 3 Ferrite Coiling average grain Generation Mechanical properties Steel sheet temperature size frequency A YS TS EI λ No. Kind (° C.) (μm) (mm/mm²) (MPa) (MPa) (%) (%) Remark 1 Hot-rolled steel sheet 580 5.6 2.0 390 450 36.2 118 Example 2 Hot-rolled steel sheet 585 6.6 17.7 383 445 37.0 113 Example 3 Zinc-coated cold- 580 5.6 2.5 370 440 37.5 120 Example rolled steel sheet 4 Zinc-coated hot-rolled 580 5.7 2.3 385 453 37.1 137 Example steel sheet 5 Hot-rolled steel sheet 585 10.3 42.8 310 441 36.2 84 Comparative example 6 Hot-rolled steel sheet 580 7.1 20.0 352 441 36.0 100 Example

EXAMPLE 2

Steel having the chemical composition given in Table 4 was prepared by melting. The steel was rolled under the conditions given in Table 5 to form hot-rolled steel sheets, each having a thickness of 2.8 mm. The steel sheets were annealed at 800° C., and were subjected to alloyed hot dip zinc-coating to prepare the steel sheets Nos. 7 through 9. The mechanical properties of these steel sheets were determined in the same procedure with that in the Example 1.

The result is shown in Table 5.

The steel sheets Nos. 7 and 8 as Examples of the present invention give superior balance of strength and ductility and balance of strength and stretch flanging performance, to the steel sheet No. 9 as a Comparative Example treated by the primary cooling speed, after the hot-rolling, of outside of the range of the present invention, and give high yield strength and excellent shock resistance. TABLE 4 Composition (wt. %) C Si Mn P S O N Cr V 0.096 0.25 1.64 0.029 0.001 0.0025 0.0026 0.20 0.055

TABLE 5 End Slab tem- Treat- perature Sec- Genera- ment Finishing Time to Primary of ondary Ferrite tion to tem- start the cooling the cooling Coiling average A Steel Heat- reduce perature primary speed primary speed tem- grain frequency Mechanical properties sheet treatment segrega- of rolling cooling (° C./ cooling (° C./ perature size (mm/ YS TS EI λ Re- No. history tion (° C.) (sec) sec) (° C.) sec) (° C.) (μm) mm²) (MPa) (MPa) (%) (%) mark 7 Casting, Applied Ar₃ − 0.60 514 643 25 556 5.5 7.0 439 719 29.3 37 E then (Ar₃ + 10) heating to 1.250° C. 8 Casting, Applied Ar₃ − 0.55 497 673 30 563 7.0 5.0 423 667 30.0 47 E then (Ar₃ + 5) heating to 1.250° C. 9 Casting, Applied Ar₃ − 0.60  30* 750 35 575 8.5 45.0 415 716 26.8 32 C then (Ar₃ + 15) heating to 1.250° C. *Outside of the range of the present invention E: Example C: Comparative example

EXAMPLE 3

The steel having the chemical composition given in Table 4 was rolled under the conditions given in Table 6 to form hot-rolled steel sheets, each having a thickness of 2.8 mm. The steel sheets were annealed at 800° C., and were subjected to alloyed hot dip zinc-coating to prepare the steel sheets Nos. 10 and 11. The dispersion of mechanical properties of these steel sheets in the width direction and in the longitudinal direction of the steel sheet coil was determined.

The result is shown in Table 6.

The steel sheet No. 10 as an Example of the present invention, which was cooled with a heat transfer coefficient of 12,000 kcal/m²h° C., gives less temperature variations in the width direction and in the longitudinal direction of the steel sheet and less variations in mechanical properties to the steel sheet No. 11 as a Comparative Example which was cooled with a heat transfer coefficient of 1,000 kcal/m²h° C., that is, by a primary cooling speed outside of the range of the present invention. The average value of tensile strength of the steel sheet No. 10 was 604 MPa. The average value of tensile strength of the steel sheet No. 11 was 625 MPa. TABLE 6 Slab Treat- Time ment Finishing to start to tem- the Primary Variations of end Secondary Coiling Variations of tensile Heat- reduce perature primary cooling temperature of the cooling tem- characteristics Steel treatment segrega- of rolling cooling speed primary cooling speed perature TS EI Re- sheet No. history tion (° C.) (sec) (° C./sec) (° C.) (° C./sec) (° C.) (MPa) (%) Structure mark 10 Casting, Applied 860 0.60 510 623-653 10 560 595-613 32-35 F + M* E then heating to 1,250° C. 11 Casting, Applied 862 1.50  30 598-675 13 557 572-680 28-33 F + M C then heating to 1,250° C. *F: Ferrite, M: Martensite E: Example C: Comparative example

Embodiment 2

The inventors of the present invention conducted detail study on the improvement of ductility of high strength steel sheets, focusing on the high strength hot dip zinc-coated steel sheets having 440 MPa or higher strength, and found that it is effective to make the structure formed during hot-rolling homogenize and refine by suppressing the formation of what is called the banded structure in which pearlite is distributed in laminar pattern, as in the above-described case, and to make the layered structure of ferrite and cementite within pearlite refine, or it is effective to establish fine pearlite lamella gap.

The method for manufacturing the high strength hot dip zinc-coated steel sheet according to the present invention was completed based on the findings. The following is the detail description of the present invention.

1. Composition

Carbon is an element necessary to assure the strength. If the C content is less than 0.01%, the strength of 440 MPa or more cannot be obtained. If the C content exceeds 0.3%, the formation of what is called the banded structure in which pearlite is distributed in layered pattern cannot be suppressed. Accordingly, the C content is specified to a range of from 0.01 to 0.3%, more preferably from 0.05 to 0.2%.

Silicon is an effective element to improve the ductility of steel. If the Si content increases, the adhesiveness of zinc coating and the surface appearance significantly degrade. Consequently, the Si content is specified to 0.7% or less.

Manganese is, similar with C, an essential element to secure strength. If, however, the Mn content is less than 1%, the strength of 440 MPa or higher level cannot be obtained. And, if the Mn content exceeds 3%, the formation of banded structure cannot be suppressed. Therefore, the Mn content is specified to a range of from 1 to 3%. When the low temperature transformed phase is not used, the Mn content is more preferably specified to a range of from 1 to 2%.

Phosphorus is a necessary element to assure strength by solid solution. If, however, the P content increases, the adhesiveness of zinc coating degrades. Consequently, the P content is specified to 0.08% or less.

Since increased content of S increases the inclusions in steel to degrade the workability, the S content is specified to 0.01% or less.

The content of sol.Al is limited to an amount that ordinary high strength steel sheet contains, or to 0.08% or less.

Similar with sol.Al, the N content is limited to an amount that ordinary high strength steel sheet contains, or to 0.007% or less.

2. Manufacturing Conditions

On applying hot-rolling to a steel slab having the above-described composition, hot-rolling is required to be carried out at temperatures of Ar₃ transformation point or above not to leave the working structure to degrade the ductility.

After completing the hot-rolling, it is necessary to apply cooling (primary cooling) with average cooling speeds of 100° C./sec or more, preferably 110° C./sec or more, within 2.5 seconds to establish homogeneous fine structure and fine pearlite lamella gap. In that case, if the cooling starts after 2.5 seconds after completed the hot-rolling, the structure and the pearlite become coarse to degrade the ductility.

Regarding the end temperature of cooling in the cooling with that cooling speed, if the cooling proceeds to 500° C. or below, large amount of low temperature transformed phase such as bainite and martensite is formed, which then becomes acicular ferrite during annealing in the continuous hot dip zinc-coating line to degrade the ductility. Therefore, the end temperature of cooling is required to exceed 500° C. If the cooling proceeds to above 700° C., the sufficiently large C diffusion rate likely forms banded structure, and the pearlite lamella gap increases to fail to attain sufficient ductility. Therefore, the end temperature of cooling is necessary to be 700° C. or above.

The steel sheet cooled to that end temperature of cooling is coiled at the end temperature of cooling or coiled at a specified temperature after cooled (secondary cooling) at normal cooling speeds of 30° C./sec or less, followed by pickled or pickled and cold-rolled, then is annealed and coated in the continuous hot dip zinc-coating line. In the continuous hot dip zinc-coating line, when the annealing is carried out at temperatures of 720° C. or above, the resolution of coarse pearlite in the colony formed during the hot-rolling or of pearlite pulverized during cold-rolling proceeds to reduce the number of origins of cracks under plastic deformation, which then improves the ductility. Particularly for increasing the strength using the slight amount of low temperature transformed phase such as bainite and austenite, the inversely transformed austenite is stably obtained by enhancing the resolution of pearlite during annealing, which gives significant increase in the ductility.

Adding to the above-described components, the addition of one or more elements selected from the group consisting of 0.005 to 0.5% Nb, 0.005 to 0.5% Ti, and 0.0002 to 0.005% B, and/or one or more elements selected from the group consisting of 0.01 to 1% V, 0.01 to 1% Cr, and 0.01 to 1% Mo is effective to obtain high strength and fine structure. The reasons of limiting the contents are described in the following.

Niobium and Ti are effective elements to obtain fine structure and high strength by precipitation hardening. To obtain these effects, the content of Nb and Ti is necessary to be 0.005% or more. If, however, the content exceeds 0.5%, the effect saturates and the ductility degrades. From the viewpoint of ductility, the content is preferably 0.1% or less.

Boron is an effective element to suppress the precipitation of ferrite and to increase the strength by forming low temperature transformed phase. To attain the effect, the B content is necessary to be 0.0002% or more. If, however, the B content exceeds 0.005%, the effect saturates and the ductility degrades.

The elements of V, Cr, and Mo are effective to increase the hardenability of steel to increase the strength. To attain the effect, the content is necessary to be 0.01% or more. If the content exceeds 1%, the effect saturates.

When the cooling starts within very short time of 0.5 second or less after the hot-rolling, the rolled structure is cooled in an incompletely recrystallized state so that the structure likely becomes non-homogeneous, thus tending to increase in the dispersion of material quality in the longitudinal direction and in the width direction of the coil. Accordingly, the cooling preferably starts after the hot-rolling in a period of from more than 0.5 second to not more than 2.5 seconds.

The present invention can be implemented by slab ingot making process or continuous casting process. For the hot-rolling, the continuous hot-rolling technology which connects sheet bars after rough-rolling can be applied. Furthermore, an induction heating unit can be used during the hot-rolling to heat the steel, for example, within a range of 200° C. or below. The effect of the present invention is not affected under alloying after zinc-coated.

EXAMPLE 1

Steels A through E having chemical compositions given in Table 7 were prepared by melting. The steels were rolled under the conditions given in Table 8 to form hot-rolled steel sheets Nos. 1 through 35, each having a thickness of 2.3 or 2.8 mm. After applying pickling, the hot-rolled steel sheets Nos. 1 through 22 and No. 35 were annealed in as-hot-rolled state, and the hot-rolled steel sheets Nos. 23 through 34 were annealed after cold-rolled at 62% of reduction in thickness, under the heat treatment conditions equivalent to the continuous hot dip zinc-coating line shown in Table 9 using a laboratory heat treatment simulator. The steel microstructure was observed, and the tensile strength (TS) and the ductility (El) in the rolling direction and in the tranversal direction to the rolling direction were determined on JIS Class 5 specimens.

The result is given in Table 9. FIG. 3 shows the relation between the primary cooling speed and the El value of the hot-rolled steel sheets Nos. 1 through 22.

When comparison is given on the same strength level, the El value improves by controlling the primary cooling speed within the range of the present invention. Particularly when the control of the time to start cooling is given in a range of more than 0.5 second and not more than 2.5 seconds, the effect becomes significant. As for the hot-rolled steel sheets Nos. 1 through 12 which comprises the (ferrite+martensite) structure, the ductility increased by about 1% compared with the hot-rolled steel sheets Nos. 13 through 22 which were strengthened by precipitation hardening on the basis of the {ferrite+pearlite (+cementite)} structure. TABLE 7 Composition (wt. %) Steel C Si Mn P S sol.Al N Other A 0.08 0.25 1.65 0.03 0.001 0.02 0.0025 Cr: 0.2, V: 0.05 B 0.065 0.1 1.5 0.012 0.003 0.019 0.0025 Nb: 0.03 C 0.180 0.02 2.5 0.015 0.001 0.03 0.0021 Cr: 0.1, Nb: 0.03 D 0.07 0.03 2.6 0.012 0.004 0.025 0.0031 Ti: 0.03, B: 0.001 E 0.05 0.15 2.3 0.018 0.0008 0.035 0.0031 —

TABLE 8 Time to End Sheet Finishing start the Primary temperature Secondary thickness Slab heating temperature primary cooling of the primary cooling Coiling after hot- temperature of rolling cooling speed cooling speed temperature rolling Steel sheet No. Steel (° C.) (° C.) (sec) (° C./sec) (° C.) (° C./sec) (° C.) (mm) Remark 1 A 1230 880 1.5  30* 600 — 600 2.3 C 2 A 1230 880 0.6  60* 600 10 550 2.3 C 3 A 1230 880 1.5  80* 600 10 550 2.3 C 4 A 1230 880 0.6 100 600 10 550 2.3 E 5 A 1230 880 2.1 150 600 10 550 2.3 E 6 A 1230 880 0.4 150 600 10 550 2.3 E 7 A 1230 880 0.6 250 600 10 550 2.3 E 8 A 1230 880 0.3 300 600 10 550 2.3 E 9 A 1230 880 0.6 400 600 10 550 2.3 E 10 A 1230 880 0.2 500 600 10 550 2.3 E 11 A 1230 880 1.3 700 600 5 550 2.3 E 12 A 1230 880 0.3 800 600 10 550 2.3 E 13 B 1230 860 0.5  15* 620 — 620 2.3 C 14 B 1230 860 1.5  20* 620 — 620 2.3 C 15 B 1230 860 1.5  80* 650 10 620 2.3 C 16 B 1230 860 0.8 120 650 10 620 2.3 E 17 B 1230 860 0.2 150 650 10 620 2.3 E 18 B 1230 860 0.6 200 650 10 620 2.3 E 19 B 1230 860 0.3 350 650 10 620 2.3 E 20 B 1230 860 1.0 450 650 10 620 2.3 E 21 B 1230 860 0.2 600 650 10 620 2.3 E 22 B 1230 860 0.7 800 650 10 620 2.3 E 23 C 1230 830 0.5  15* 620 — 620 2.8 C 24 C 1230 830 0.5  80* 650 5 620 2.8 C 25 C 1230 830 0.7 200 650 5 620 2.8 E 26 C 1230 830 0.7 600 650 5 620 2.8 E 27 D 1230 850 0.5  20* 530 — 530 2.8 C 28 D 1230 850 0.8 300 580 10 530 2.8 E 29 E 1230 850 1.3  10* 600 — 600 2.8 C 30 E 1230 850 0.3 150 650 5 600 2.8 E 31 E 1230 850 0.3 300 650 5 600 2.8 E 32 E 1230 850 0.3 600 650 5 600 2.8 E 33 E 1230 850 1.3 400 650 5 600 2.8 E 34 E 1230 850 1.3 600 650 5 600 2.8 E 35 A 1230 880 3.0* 500 600 10 550 2.3 C *Outside of the range of the present invention E: Example C: Comparative example

TABLE 9 Condition of hot dip zinc- Reduction in coating Tensile Primary cooling thickness during Final sheet Soaking characteristics Steel speed cold-rolling thickness temperature Alloying Micro- TS EI sheet No. Steel (° C./sec) (%) (mm) (° C.) performance structure (MPa) (%) Remark 1 A  30* — 2.3 800 ◯ F + M 620 30.0 C 2 A  60* — 2.3 800 ◯ F + M 618 30.0 C 3 A  80* — 2.3 800 ◯ F + M 621 30.2 C 4 A 100 — 2.3 800 ◯ F + M 620 30.5 E 5 A 150 — 2.3 800 ◯ F + M 623 31.5 E 6 A 150 — 2.3 800 ◯ F + M 619 31.2 E 7 A 250 — 2.3 800 ◯ F + M 620 32.3 E 8 A 300 — 2.3 800 ◯ F + M 622 32.0 E 9 A 400 — 2.3 800 ◯ F + M 621 32.8 E 10 A 500 — 2.3 800 ◯ F + M 620 32.2 E 11 A 700 — 2.3 800 ◯ F + M 625 33.0 E 12 A 800 — 2.3 800 ◯ F + M 622 32.3 E 13 B  15* — 2.3 750 X F + P (or+C) 599 28.0 C 14 B  20* — 2.3 750 X F + P (or+C) 600 28.0 C 15 B  80* — 2.3 750 X F + P (or+C) 602 28.0 C 16 B 120 — 2.3 750 X F + P (or+C) 600 28.5 E 17 B 150 — 2.3 750 X F + P (or+C) 598 28.5 E 18 B 200 — 2.3 750 X F + P (or+C) 603 29.3 E 19 B 350 — 2.3 750 X F + P (or+C) 600 29.2 E 20 B 450 — 2.3 750 X F + P (or+C) 597 29.7 E 21 B 600 — 2.3 750 X F + P (or+C) 602 29.5 E 22 B 800 — 2.3 750 X F + P (or+C) 604 29.9 E 23 C  15* 62 1.2 830 ◯ F + M 1010 15.0 C 24 C  80* 62 1.2 830 ◯ F + M 1006 15.0 C 25 C 200 62 1.2 830 ◯ F + M 1008 16.0 E 26 C 600 62 1.2 830 ◯ F + M 1012 17.0 E 27 D  20* 62 1.2 800 ◯ F + M 810 21.0 C 28 D 300 62 1.2 800 ◯ F + M 815 22.5 E 29 E  10* 62 1.2 780 X F + B + M 599 29.0 C 30 E 150 62 1.2 780 X F + B + M 603 29.5 E 31 E 300 62 1.2 780 X F + B + M 601 30.0 E 32 E 600 62 1.2 780 X F + B + M 600 30.0 E 33 E 400 62 1.2 780 X F + B + M 597 30.5 E 34 E 600 62 1.2 780 X F + B + M 602 31.5 E 35 A 500 — 2.3 800 ◯ F + M 621 30.0 C *Outside of the range of the present invention, F: Ferrite, M: Martensite, P: Pearlite, C: Cementite, B: Bainite E: Example C: Comparative example

Embodiment 3

As described above, when the high strength steel sheets having strengths of 340 MPa or more are manufactured, the cracks likely occur during the hot-rolling to degrade the surface properties, which results in reduced yield. The surface defects caused from the cracks occurred in hot-rolling step presumably come from the occurrence of cracks owing to red shortness appeared on the surface or below the surface of the slab under bending deformation during the continuous casting, which cracks significantly develop in the succeeding rolling to result in the surface defects. In normal practice, the surface defects are prevented by trimming the slab. The slab trimming induces cost increase. And the direct rolling process which cannot implement the slab trimming cannot be applied.

The inventors of the present invention investigated the methods to maintain the above-described excellent workability such as stretch flanging performance and ductility, and the characteristics such as shock resistance, and to prevent the surface defects caused from the cracks occurred during the hot-rolling, and found that the high strength steel sheets having excellent surface properties can be obtained, even without applying slab trimming, by controlling the content of P, O, S, N, and Sn and the ratio of Mn/S in the steel, and furthermore, at need, by adding an adequate amount of Ca.

The method for manufacturing the high strength steel sheet according to the present invention was completed on the basis of these findings. The detail is described in the following.

1. Composition

Carbon is a necessary element to assure strength. If the C content is less than 0.05%, the crack occurrence on the surface or beneath the surface of slab during continuous casting cannot be suppressed. If the C content exceeds 0.2%, the workability degrades. Accordingly, the C content is specified to a range of from 0.05 to 0.2%, preferably from 0.05 to 0.1%.

Silicon is a necessary element to assure strength. If the Si content exceeds 0.15%, the surface properties degrade. Consequently, the Si content is specified to 0.15% or less.

Manganese is an effective element that can suppress the occurrence of cracks on the surface or beneath the surface of slab during continuous casting. If the Mn content is less than 0.4%, the effect cannot be attained. If the Mn content exceeds 2.0%, the workability degrades. Therefore, the Mn content is specified to a range of from 0.4 to 2.0%.

Phosphorus is a harmful element which enhances the crack occurrence on the surface or beneath the surface of slab during continuous casting. If the P content exceeds 0.025%, the crack occurrence becomes significant on the surface or beneath the surface of slab during continuous casting, and the frequency of crack occurrence in hot-rolling step increases. Accordingly, the P content is specified to 0.025% or less, preferably 0.010% or less.

Oxygen is a harmful element which enhances the crack occurrence on the surface or beneath the surface of slab during continuous casting. If the O content exceeds 0.005%, the slab crack occurrence becomes significant during continuous casting, and the workability of the steel sheet degrades. Accordingly, the O content is specified to 0.005% or less.

Sulfur is a harmful element which significantly enhances the crack occurrence on the surface or beneath the surface of slab during continuous casting, and which, even if no slab crack occurred, induces cracks during hot-rolling to degrade the surface properties of the steel sheet and to degrade the workability thereof. If the S content exceeds 0.01%, the occurrence of slab cracks becomes significant during continuous casting, and the workability of steel sheet degrades. Therefore, the S content is specified to 0.01% or less, preferably 0.005% or less, more preferably 0.001% or less.

Nitrogen is an element which should be reduced in the content thereof to suppress the crack occurrence during hot-rolling and to improve the workability of steel sheet. If the N content exceeds 0.006%, the crack occurrence during hot-rolling and the degradation in workability are induced. Accordingly, the N content is specified to 0.006% or less, preferably 0.005% or less.

Tin is an extremely harmful element which significantly enhances the crack occurrence on the surface or beneath the surface of slab during continuous casting. In recent years, however, there are increased uses of scrap in steel making, and the Sn content has increased. If the Sn content exceeds 0.004%, the crack occurrence on the surface or beneath the surface of slab during the continuous casting particularly becomes significant, which induces increased frequency of crack occurrence during hot-rolling. Therefore, the Sn content is specified to 0.004% or less.

Adding to the above-described limitations of components, Mn/S is specified to not less than 50 because the Mn/S below 50 significantly enhances the crack occurrence on the surface or beneath the surface of slab during the continuous casting.

2. Manufacturing Conditions

With the steel slabs having the above-described compositions, the occurrence of surface defects caused from the cracks on the surface or beneath the surface of slab during the continuous casting can be suppressed even when the slab is reheated and hot-rolled after the continuous casting without applying the slab trimming, or even when the slab is directly hot-rolled (direct rolling) without applying reheating. When, before the direct rolling, supplemental heating to 1,250° C. or below is applied, the brittleness of grain boundaries caused from sulfide is suppressed, and high strength steel sheet having further excellent surface properties and excellent workability is obtained. Since the method according to the present invention does not need slab trimming, the manufacturing cost is reduced and the direct rolling process can be applied.

The hot-rolling is necessary to be conducted at temperatures of Ar₃ transformation point or above to refine the ferritic grains and to improve the workability of the steel sheet.

After completed the hot-rolling, cooling is necessary to be given at cooling speeds of from 20 to 2,000° C./sec, preferably from 50 to 2,000° C./sec, more preferably from 120 to 2,000° C./sec to refine the ferritic grains and the pearlite after the transformation to improve the workability of the steel sheet.

When the steel sheets which were cooled at above-described cooling speeds are coiled at temperatures of below 400° C., the formation of low temperature transformed phase degrades the balance of strength and ductility. And, when the coiling is done at temperatures of above 700° C., the coarse pearlite which is harmful to ductility is generated. Therefore, the coiling is necessary to be done at temperatures of from 400 to 700° C.

Adding to the above-described components, if 0.005% or less of Ca is added, the crack occurrence on the surface or beneath the surface of slab during continuous casting is more surely suppressed. The reason of limiting the Ca content to 0.005% or less is that the Ca content of more than 0.005% increases the frequency of crack occurrence beneath the surface of slab.

When the reduction in thickness at the final stand during the hot-rolling is regulated to a range of from 8 to 30%, good coil shape is attained and improved workability of steel sheet is obtained owing to the sufficiently refined ferritic grains.

After completed the hot-rolling, start of the cooling within 1.0 second, preferably within 0.5 second suppresses the growth of austenitic grains after the rolling and before the transformation, thus provides a steel sheet having further excellent workability. Shorter time to start for cooling gives stronger effect. Since, however, the time to start for cooling within 0.1 second cannot be actualized because of the limitations of facilities, the lower limit of the time to start for cooling is specified to more than 0.1 second.

The high strength steel sheet having excellent surface properties and workability can also be obtained by applying normal method of cold-rolling and annealing to a coiled hot-rolled steel sheet to form a cold-rolled steel sheet.

On applying the present invention, when the whole of sheet bar or the edge portions thereof after the rough-rolling is heated before the finish-rolling, homogeneous workability is attained over the whole area of the coil. What is called the continuous hot-rolling technology which uses a coil box to apply hot-rolling while connecting the sheet bar can be applied to the present invention. In that case, the sheet bar heating may be done inside of the coil box, before or after the coil box, in the rough-rolling mills, or after the rough-rolling mill.

EXAMPLE 1

Steels Nos. 1 through 12 having the chemical compositions given in Table 10 were prepared by melting. The steels were hot-rolled under the conditions given in Table 11 to form hot-rolled steel sheets Nos. 1 through 12, each having a thickness of 3.0 mm. The tensile strength (TS) and the hole expanding rate (λ) were determined on each steel sheet using the above-described method. The surface properties of each of the steel sheets were visually inspected on the basis of the number of surface defects generated on the hot-rolled steel sheet coil, giving the three evaluation grades:

-   ⊚: zero (Present invention) -   ◯: more than zero and not more than 2 (Present invention) -   x: more than 2 (outside of the Present invention)

The result is shown in Table 11. FIG. 4 shows the relation between TS, λ, and surface properties.

The hot-rolled steel sheets Nos. 1 through 4 which are the Examples of the present invention give excellent surface properties. The hole expanding rate in the Examples of the present invention is superior to the hot-rolled steel sheets Nos. 5 through 12 which are Comparative Examples on the basis of the same strength level. TABLE 10 Steel Composition (wt. %) No. C Si Mn S P O N Sn Mn/S Ti Nb B V 1 0.0630 0.01 0.74 0.001 0.006 0.0024 0.0021 0.0030 740 — — — — 2 0.0700 0.02 0.63 0.003 0.017 0.0021 0.0028 0.0020 210 0.052 — — — 3 0.1140 0.15 0.50 0.004 0.012 0.0025 0.0025 0.0010 125 0.015 0.020 — — 4 0.1600 0.02 0.71 0.003 0.017 0.0019 0.0038 0.0020 237 — — 0.001 0.020 5 0.1810 0.02 0.30* 0.003 0.019 0.0020 0.0037 0.0020 100 — — — — 6 0.0500 0.02 2.10* 0.003 0.015 0.0023 0.0028 0.0030 700 — — — — 7 0.1670 0.03 0.49 0.015* 0.010 0.0060* 0.0024 0.0040  33* — — — — 8 0.1230 0.01 0.56 0.004 0.028* 0.0027 0.0067* 0.0020 140 — — — — 9 0.1700 0.02 0.65 0.003 0.015 0.0055* 0.0020 0.0055* 217 — — — — 10 0.1710 0.01 0.51 0.003 0.017 0.0031 0.0072* 0.0020 170 — — — — 11 0.1650 0.02 0.49 0.003 0.015 0.0028 0.0039 0.0050* 163 — — — — 12 0.1580 0.02 0.40 0.010 0.014 0.0035 0.0040 0.0040  40* — — — — *Outside of the range of the present invention

TABLE 11 Manufacturing condition Mechanical Steel Coiling properties sheet Steel Slab heat- Cooling speed temperature Surface λ TS No. No. treatment history (° C./sec) (° C.) property (%) (MPa) Remark 1 1 Direct rolling 45 620 ◯ 133 461 Example 2 2 Heating to 1,150° C. 60 572 ⊚ 110 510 Example 3 3 Heating to 1,150° C. 110 563 ⊚ 105 550 Example 4 4 Direct rolling 180 550 ◯ 121 590 Example 5 5 Direct rolling 40 540 X 125 440 Comparative Example 6 6 Direct rolling 46 550 ◯ 85 540 Comparative Example 7 7 Direct rolling 40 551 X 58 451 Comparative Example 8 8 Direct rolling 35 521 X 115 430 Comparative Example 9 9 Direct rolling 45 535 X 91 466 Comparative Example 10 10 Direct rolling 41 532 X 85 455 Comparative Example 11 11 Direct rolling 35 510 X 104 448 Comparative Example 12 12 Direct rolling 40 516 X 110 431 Comparative Example

EXAMPLE 2

The steels Nos. 1 and 2 shown in Table 10 were hot-rolled under the condition given in Table 12 to prepare hot-rolled steel sheets Nos. 13 through 20, each having a sheet thickness of 3.0 mm. The same evaluation with that in Example 1 was given.

The result is shown in Table 12. FIG. 5 shows the relation between TS, λ, and surface properties.

The hot-rolled steel sheets Nos. 14 through 16 and 18 through 20 which are the Examples of the present invention give excellent surface properties. The hole expanding rate in the Examples of the present invention is superior to the hot-rolled steel sheets Nos. 13 and 17 which are Comparative Examples on the basis of the same strength level. TABLE 12 Manufacturing condition Mechanical Steel Coiling properties sheet Steel Slab heat- Cooling speed temperature Surface λ TS No. No. treatment history (° C./sec) (° C.) property (%) (MPa) Remark 13 1 Heating to 1,150° C.  15* 605 ⊚ 103 435 Comparative Example 14 1 Heating to 1,150° C.  45 620 ⊚ 133 461 Example 15 1 Heating to 1,150° C. 126 618 ⊚ 128 502 Example 16 1 Heating to 1,150° C. 320 624 ⊚ 124 558 Example 17 2 Direct rolling  13* 621 ◯ 92 474 Comparative Example 18 2 Direct rolling  60 572 ◯ 110 510 Example 19 2 Direct rolling 163 615 ◯ 106 562 Example 20 2 Direct rolling 360 584 ◯ 104 612 Example *Outside of the range of the present invention

EXAMPLE 3

The steels Nos. 1 and 12 shown in Table 10 were hot-rolled under the condition given in Table 13 to prepare hot-rolled steel sheets Nos. 21 through 32, each having a sheet thickness of 3.0 mm. The same evaluation with that in Example 1 was given.

The result is shown in Table 13. FIG. 6 shows the relation between TS, λ, and surface properties.

The hot-rolled steel sheets Nos. 21 through 24 which are the Examples of the present invention give excellent surface properties. The hole expanding rate in the Examples of the present invention is superior to the hot-rolled steel sheets Nos. 25 and 32 which are Comparative Examples on the basis of the same strength level. Furthermore, the shape of the hot-rolled coil in the Examples of the present invention was excellent. TABLE 13 Manufacturing condition Mechanical Steel Final reduction Time to start Cooling Coiling properties sheet Steel Slab heat- in thickness cooling speed temperature Surface λ TS No. No. treatment history (%) (sec) (° C./sec) (° C.) Coil shape properties (%) (MPa) Remark 21 1 Heating to 1,200° C. 10 0.2 45 620 Good ◯ 135 460 Example 22 2 Heating to 1,200° C. 15 0.2 60 570 Good ⊚ 115 511 Example 23 3 Heating to 1,200° C. 15 0.5 180 563 Good ⊚ 121 590 Example 24 4 Heating to 1,200° C. 20 1.3 180 552 Good ◯ 105 550 Example 25 5 Direct rolling 10 1.5 40 540 Good X 125 440 Comparative example 26 6 Direct rolling 35 1.3 46 551 Significant ◯ 85 550 Comparative edge wave example 27 7 Direct rolling 10 1.3 40 551 Good X 58 451 Comparative example 28 8 Direct rolling 10 1.2 35 521 Good X 115 430 Comparative example 29 9 Direct rolling 15 1.5 45 540 Good X 91 466 Comparative example 30 10 Direct rolling 15 1.5 41 532 Good X 85 455 Comparative example 31 11 Direct rolling 15 1.5 35 510 Good X 104 448 Comparative example 32 12 Direct rolling 15 1.5 40 516 Good X 110 431 Comparative example 

1. A method for manufacturing high strength hot dip zinc-coated steel sheet comprising the steps of: hot-rolling a steel slab consisting essentially of 0.01 to 0.3% C, 0.7% or less Si, 1 to 3% Mn, 0.08% or less P, 0.01% or less S, 0.08% or less sol.Al, and 0.007% or less N, by weight, at temperatures of Ar₃ transformation point or above; cooling the hot-rolled steel sheet within 2.5 seconds down to the temperatures of from above 500° C. to 700° C. at average cooling speeds of 100° C./sec or more, followed by coiling the cooled steel sheet; and pickling the coiled steel sheet, or pickling the coiled steel sheet and cold-rolling the pickled steel sheet, then annealing thereto in a continuous hot dip zinc-coating line at temperatures of 720° C. or above to perform zinc coating.
 2. The method for manufacturing high strength hot dip zinc-coated steel sheet of claim 1, wherein the steel slab further contains at least one element selected from the group consisting of 0.005 to 0.5% Nb, 0.005 to 0.5% Ti, and 0.0002 to 0.005% B.
 3. The method for manufacturing high strength hot dip zinc-coated steel sheet of claim 1, wherein the steel slab further contains at least one element selected from the group consisting of 0.01 to 1% V, 0.01 to 1% Cr, and 0.01 to 1% Mo.
 4. The method for manufacturing high strength hot dip zinc-coated steel sheet of claim 2, wherein the steel slab further contains at least one element selected from the group consisting of 0.01 to 1% V, 0.01 to 1% Cr, and 0.001 to 1% Mo.
 5. The method for manufacturing high strength hot dip zinc-coated steel sheet of claim 1, wherein the steel sheet after completed the hot-rolling is cooled in a period of from more than 0.5 second to 2.5 seconds at average cooling speeds of 100° C./sec or more.
 6. The method for manufacturing high strength hot dip zinc-coated steel sheet of claim 2, wherein the steel sheet after completed the hot-rolling is cooled in a period of from more than 0.5 second to 2.5 seconds at average cooling speeds of 100° C./sec or more.
 7. The method for manufacturing high strength hot dip zinc-coated steel sheet of claim 3, wherein the steel sheet after completed the hot-rolling is cooled in a period of from more than 0.5 second to 2.5 seconds at average cooling speeds of 100° C./sec or more.
 8. The method for manufacturing high strength hot dip zinc-coated steel sheet of claim 4, wherein the steel sheet after completed the hot-rolling is cooled in a period of from more than 0.5 second to 2.5 seconds at average cooling speeds of 100° C./sec or more. 